Glass-ceramic compositions and laminated glass articles incorporating the same

ABSTRACT

According to one embodiment, a glass-ceramic composition may include from about 60 mol. % to about 75 mol. % SiO2; from about 5 mol. % to about 10 mol. % AI2O3; from about 2 mol. % to about 20 mol. % alkali oxide R2O, the alkali oxide R2O including Li2O and Na2O; and from 0 mol. % to about 5 mol. % alkaline earth oxide RO, the alkaline earth oxide RO including MgO. A ratio of Al2O3 (mol. %)) to the sum of (R2O (mol. %)+RO (mol. %)) may be less than 1 in the glass-ceramic composition. A major crystalline phase of the glass-ceramic composition may be Li2Si2O5. A liquidus viscosity of the glass-ceramic composition may be greater than 35 kP. The glass-ceramic composition may be used to form the glass clad layer(s) of a laminated glass article.

This application claims the benefit of priority to International Application No PCT/US2015/057928, filed on Oct. 29, 2015, which claims the benefit of priority to U.S. Application No. 62/072,673, filed on Oct. 30, 2014, the content of each of which is incorporated herein by reference in its entirety.

BACKGROUND Field

The present specification generally relates to glass-ceramic compositions and to laminated glass articles incorporating glass-ceramic compositions.

Technical Background

Glass articles, such as cover glasses, glass backplanes and the like, are employed in both consumer and commercial electronic devices such as LCD and LED displays, computer monitors, automated teller machines (ATMs) and the like. Some of these glass articles may include “touch” functionality which necessitates that the glass article be contacted by various objects including a user's fingers and/or stylus devices and, as such, the glass must be sufficiently robust to endure regular contact without damage. Moreover, such glass articles may be incorporated in portable electronic devices, such as mobile telephones, personal media players, and tablet computers. The glass articles incorporated in these devices may be susceptible to damage during transport and/or use of the associated device. Accordingly, glass articles used in electronic devices may require enhanced strength to be able to withstand not only routine “touch” contact from actual use, but also incidental contact and impacts which may occur when the device is being transported.

SUMMARY

According to one embodiment, a glass-ceramic composition may include from about 60 mol. % to about 75 mol. % SiO₂; from about 5 mol. % to about 10 mol. % Al₂O₃; from about 2 mol. % to about 20 mol. % alkali oxide R₂O, the alkali oxide R₂O comprising Li₂O and Na₂O; and from about 0 mol. % to about 5 mol. % alkaline earth oxide RO, the alkaline earth oxide RO comprising MgO. A ratio of Al₂O₃ (mol. %) to the sum of (R₂O (mol. %)+RO (mol. %)) may be less than 1 in the glass-ceramic composition. A major crystalline phase of the glass-ceramic composition may be Li₂Si₂O₅. A liquidus viscosity of the glass-ceramic composition may be greater than 35 kP.

In another embodiment, a laminated glass article may include a glass core layer having a core coefficient of thermal expansion CTE_(C). At least one glass clad layer may be directly fused to the glass core layer. The at least one glass clad layer may include from about 60 mol. % to about 75 mol. % SiO₂; from about 5 mol. % to about 10 mol. % Al₂O₃; from about 2 mol. % to about 20 mol. % alkali oxide R₂O, the alkali oxide R₂O comprising Li₂O and Na₂O; from about 0 mol. % to about 5 mol. % alkaline earth oxide RO, the alkaline earth oxide RO comprising MgO. A ratio of Al₂O₃ (mol. %) to the sum of (R₂O (mol. %)+RO (mol. %)) in the glass clad layer may be less than 1. A major crystalline phase of the at least one glass clad layer may be Li₂Si₂O₅. The at least one glass clad layer may have a clad coefficient of thermal expansion CTE_(CL), that is greater than or equal to 20×10⁻⁷/° C. and less than or equal to about 70×10⁻⁷/° C. and less than the core coefficient of thermal expansion CTE_(C).

Additional features and advantages of the glass-ceramic compositions described herein will be set forth in the detailed description which follows, and in part will be readily apparent to those skilled in the art from that description or recognized by practicing the embodiments described herein, including the detailed description which follows, the claims, as well as the appended drawings.

It is to be understood that both the foregoing general description and the following detailed description describe various embodiments and are intended to provide an overview or framework for understanding the nature and character of the claimed subject matter. The accompanying drawings are included to provide a further understanding of the various embodiments, and are incorporated into and constitute a part of this specification. The drawings illustrate the various embodiments described herein, and together with the description serve to explain the principles and operations of the claimed subject matter.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 schematically depicts a cross section of a laminated glass article according to one or more embodiments shown and described herein; and

FIG. 2 schematically depicts an apparatus for forming a laminated glass article according to one or more embodiments shown and described herein.

DETAILED DESCRIPTION

Reference will now be made in detail to various embodiments of glass-ceramic compositions and laminated glass articles formed therefrom. Whenever possible, the same reference numerals will be used throughout the drawings to refer to the same or like parts. According to one embodiment a glass-ceramic composition may include may include from about 60 mol. % to about 75 mol. % SiO₂; from about 5 mol. % to about 10 mol. % Al₂O₃; from about 2 mol. % to about 20 mol. % alkali oxide R₂O, the alkali oxide R₂O comprising Li₂O and Na₂O; and from about 0 mol. % to about 5 mol. % alkaline earth oxide RO, the alkaline earth oxide RO comprising MgO. A ratio of Al₂O₃ (mol. %) to the sum of (R₂O (mol. %)+RO (mol. %)) may be less than 1 in the glass-ceramic composition. A major crystalline phase of the glass-ceramic composition may be Li₂Si₂O₅. A liquidus viscosity of the glass-ceramic composition may be greater than 35 kP. Various embodiments of glass-ceramic compositions and laminated glass articles incorporating the same will be described in further detail herein with specific reference to the appended drawings.

The term “liquidus viscosity,” as used herein, refers to the shear viscosity of the glass-ceramic composition at its liquidus temperature.

The term “CTE,” as used herein, refers to the coefficient of thermal expansion of a glass or glass-ceramic composition averaged over a temperature range from about 20° C. to about 300° C.

The term “substantially free,” when used to described the absence of a particular oxide component in a glass or glass-ceramic composition, means that the component is present in the glass or glass-ceramic composition as a contaminant in a trace amount of less than 0.1 mol. %.

In the embodiments of the glass-ceramic compositions described herein, the concentration of constituent components (e.g., SiO₂, Al₂O₃, Na₂O and the like) are given in mole percent (mol. %) on an oxide basis, unless otherwise specified.

The glass-ceramic compositions described herein have properties, such as the liquidus viscosity, which make the glass-ceramic compositions particularly well suited for use with fusion forming processes, such as the fusion down draw process and/or the fusion lamination process. These properties are attributable to the specific compositions of the glasses.

As will be described in further detail herein, laminated glass articles may be formed by fusing one or more glass clad layers to a glass core layer. When strengthening of the laminated glass article is desired, the glass clad layer(s) and the glass core layer may have different coefficients of thermal expansion (CTE) such that, upon cooling, compressive stress develops in the glass clad layers(s).

Various processes may be utilized to produce laminated glass articles, including the fusion lamination process which yields a continuous ribbon of laminated glass. Discrete laminated glass articles may be singulated from the continuous ribbon of laminated glass for incorporation in other devices. If the compressive stress develops in the clad glass layer(s) of the continuous ribbon of laminated glass prior to singulation, the singulation process may be difficult due to the increased strength of the laminated glass from the presence of the compressive stress, potentially resulting in unwanted damage to the continuous ribbon of laminated glass and/or the discrete laminated glass articles.

However, the timing of the development of the compressive stress can be controlled by utilizing glass-ceramic compositions to form at least the clad glass layers. Glass-ceramic compositions may have a first coefficient of thermal expansion pre-ceramming (CTE_(PC)) and a second coefficient of thermal expansion after ceramming (CTE_(AC)) which allows the timing of the introduction of compressive stress to be controlled based on the ceramming process. For example, the glass clad layers may be formed from a glass-ceramic composition which has a pre-ceramming CTE_(PC) that is approximately the same as the coefficient of thermal expansion of the glass core layer such that the ribbon of laminated glass may be initially formed without introducing compressive stress in the glass clad layer(s) due to the coefficient of thermal expansion mismatch between the glass clad layers(s) and the glass core layer. This allows for the discrete laminated glass articles to be readily singulated from the continuous ribbon of laminated glass without damaging either the ribbon or the discrete laminated glass articles. Thereafter, the discrete laminated glass articles may be cerammed (i.e., heat treated) to form a ceramic crystal phase in the glass clad layers, thereby lowering the coefficient of thermal expansion of the glass clad layers to CTE_(AC) which, in turn, causes compressive stress to develop in the surface of the glass clad layers. The glass-ceramic compositions described herein have a pre-ceramming CTE_(PC) which is greater than the post ceramming CTE_(AC) and, as such are well suited for use as a glass clad layer of a strengthened laminated glass article.

In the embodiments of the glass-ceramic compositions described herein SiO₂ is the largest constituent of the composition and, as such, SiO₂ is the primary constituent of the glass network formed from the glass-ceramic compositions. Pure SiO₂ has a relatively low CTE. However, pure SiO₂ has an extremely high melting point. Accordingly, if the concentration of SiO₂ in the glass-ceramic compositions described herein is too high, the formability of the glass-ceramic composition may be diminished as higher concentrations of SiO₂ increase the difficulty of melting the glass which, in turn, adversely impacts the formability of the glass.

In the embodiments described herein, the glass-ceramic compositions generally comprise SiO₂ in a concentration greater than or equal to about 60 mol. % and less than or equal to about 75 mol. % in order to facilitate fusion forming the glass-ceramic compositions. In some embodiments, the concentration of SiO₂ in the glass-ceramic composition is greater than or equal to about 68 mol. % and less than or equal to about 75 mol. %. In still other embodiments, the amount of SiO₂ in the glass-ceramic composition is greater than or equal to about 70 mol. % and less than or equal to about 74 mol. %. In some other embodiments, the glass-ceramic composition comprises SiO₂ in a concentration from about 71 mol. % to about 73 mol. %.

The glass-ceramic compositions described herein also comprise Al₂O₃. Al₂O₃ serves as a glass network former, similar to SiO₂. Like SiO₂, Al₂O₃ increases the viscosity of the glass-ceramic composition due to its tetrahedral coordination in a glass melt formed from the glass-ceramic composition. However, when the concentration of Al₂O₃ is balanced against the concentration of SiO₂ and the concentration of alkali and alkaline earth oxides in the glass-ceramic composition, Al₂O₃ can reduce the liquidus temperature of the glass melt, thereby enhancing the liquidus viscosity and improving the compatibility of the glass-ceramic composition with certain forming processes such as the fusion forming process.

In the embodiments described herein, the concentration of Al₂O₃ in the glass-ceramic compositions is greater than or equal to about 5 mol. % and less than or equal to about 12 mol. %. In some embodiments, the concentration of Al₂O₃ in the glass-ceramic compositions may be greater than or equal to about 5 mol. % and less than or equal to about 10 mol. %. In some other embodiments, the concentration of Al₂O₃ in the glass-ceramic compositions may be greater than or equal to about 6 mol. % and less than or equal to about 10 mol. %. In some other embodiments, the concentration of Al₂O₃ in the glass ceramic compositions may be greater than or equal to about 7 mol. % and less than or equal to about 10 mol. %.

The glass-ceramic compositions described herein also include alkali oxide R₂O where R is at least one of a Group I metal including, without limitation, Li, Na, K, Rb, Cs, or combinations thereof. In the embodiments described herein the alkali oxide lowers the melting temperature and the liquidus temperature of the glass, thereby improving the formability of the glass-ceramic compositions. However, relative to other oxides included in the glass, alkali oxides increase the CTE of the glass-ceramic compositions while simultaneously improving the ion-exchange performance. In general, the substitution of K₂O for Na₂O generally increases the CTE of the glass while the substitution of Li₂O for Na₂O decreases the CTE. Accordingly, the presence of smaller alkali ions in the glass causes a smaller increase in the CTE.

Additions of alkali oxide R₂O also facilitate ion-exchange strengthening the glass-ceramic compositions due to their relatively high mobility in the glass. For example, smaller ions in a glass article formed from the glass-ceramic composition, such as Li⁺ ions and Na⁺ ions, may be exchanged for larger ions, such as K⁺ ions, in a molten salt bath, thereby creating compressive stress in the surface of the glass article formed from the glass-ceramic composition.

Further, the addition of the specific alkali oxide Li₂O to the glass-ceramic compositions facilitates the formation of Li₂Si₂O₅ (lithium disilicate) in the glass network upon ceramming (i.e., upon heat treatment) after initial formation. Li₂Si₂O₅ is the primary crystal phase of the glass-ceramic compositions described herein. The formation of Li₂Si₂O₅ in the glass-ceramic compositions lowers the coefficient of thermal expansion of the as-formed glass-ceramic compositions, making the glass-ceramic compositions particularly useful as the clad glass layers of a laminated glass article when strengthening is desired.

In the embodiments described herein, the alkali oxide R₂O includes at least one of Li₂O or Na₂O and, in some embodiments, may include K₂O. In the embodiments described herein, Na₂O may be present in the glass-ceramic compositions in a concentration greater than or equal to about 1 mol. % and less than or equal to about 10 mol. % or even a concentration greater than or equal to about 2 mol. % and less than or equal to about 9 mol. %. In some embodiments, Na₂O may be present in the glass-ceramic compositions in a concentration greater than or equal to about 3 mol. % and less than or equal to about 9 mol. % or even a concentration greater than or equal to about 4 mol. % and less than or equal to about 8 mol. %. In some embodiments, Na₂O may be present in the glass-ceramic compositions in a concentration greater than or equal to about 5 mol. % and less than or equal to about 8 mol. %.

Li₂O may be present in the glass-ceramic compositions in a concentration greater than or equal to about 1 mol. % and less than or equal to about 10 mol. % or even a concentration greater than or equal to about 2 mol. % and less than or equal to about 8 mol. %. In some embodiments, Li₂O may be present in the glass-ceramic compositions in a concentration greater than or equal to about 3 mol. % and less than or equal to about 7 mol. % or even a concentration greater than or equal to about 4 mol. % and less than or equal to about 6 mol. %.

K₂O may be present in the glass-ceramic compositions in a concentration greater than or equal to about 0 mol. % and less than or equal to about 10 mol. % or even a concentration greater than or equal to about 0.5 mol. % and less than or equal to about 8 mol. %. In some embodiments, K₂O may be present in the glass-ceramic compositions in a concentration greater than or equal to about 1 mol. % and less than or equal to about 7 mol. % or even a concentration greater than or equal to about 1 mol. % and less than or equal to about 5 mol. %. In some other embodiments, K₂O may be present in the glass-ceramic compositions in a concentration greater than or equal to about 2 mol. % and less than or equal to about 4 mol. %. In still other embodiments, the glass-ceramic compositions may be substantially free of K₂O.

In some embodiments, the glass-ceramic compositions described herein may further include alkaline earth oxide RO, where R is an alkaline earth metal including, without limitation one or more of Mg, Ca, Ba, and Sr. The alkaline earth oxide RO improves the melting behavior of the glass-ceramic compositions but may also increase the average coefficient of thermal expansion of the compositions. While, the alkaline earth oxides do not increase the average coefficient of thermal expansion of the glass-ceramic compositions as much as the alkali oxides contained in the glass-ceramic compositions, they do decrease the mobility of alkali ions in the glass thereby decreasing the ion-exchangeability of the glass-ceramic compositions. Accordingly, in the embodiments described herein, additions of the alkaline earth oxide RO are limited. Indeed, in some embodiments, the glass-ceramic compositions are substantially free of alkaline earth oxides while in others the total concentration of alkaline earth oxides is less than or equal to about 5 mol. %. That is, in the embodiments described herein, the concentration of alkaline earth oxides in the glass-ceramic compositions may be greater than or equal to 0 mol. % and less than or equal to about 5 mol. %.

It has been found that the specific alkaline earth oxide MgO minimizes the adverse impact on alkali diffusivity and, as such, only minimally decreases the ion-exchange performance of the glass-ceramic compositions. Moreover, MgO does not increase the average CTE of the glass-ceramic compositions as much as other alkaline earth oxides such as, for example, CaO and BaO. Accordingly, in some embodiments of the glass-ceramic compositions which include alkaline earth oxide RO, the alkaline earth oxide comprises MgO. In these embodiments, MgO may be present in the glass-ceramic compositions in an amount which is greater than or equal to 0 mol. % and less than or equal to about 5 mol. %. In some of these embodiments, MgO may be present in the glass-ceramic compositions in an amount which is less than or equal to about 4 mol. % such as less than or equal to about 3 mol. % or even less than or equal to about 2 mol. %.

In some embodiments, the glass-ceramic compositions may be substantially free of alkaline earth oxides RO.

In some embodiments, TiO₂ may be included in the glass-ceramic compositions. Additions of TiO₂ act as a nucleating agent and aid in the formation of the Li₂Si₂O₅ primary crystal phase upon ceramming. Further, additions of TiO₂ to the glass-ceramic compositions also results in the nucleation and formation of a secondary crystal phase upon ceramming, specifically rutile (TiO₂). In the embodiments described herein, TiO₂ is present in the glass-ceramic compositions in a concentration greater than or equal to 0 mol. % and less than or equal to 4 mol. %. In some embodiments, the concentration of TiO₂ in the glass-ceramic compositions may be greater than or equal to 1 mol. % and less than or equal to 4 mol. %. In some embodiments, the concentration of TiO₂ in the glass-ceramic compositions may be greater than or equal to 1 mol. % and less than or equal to 3 mol. %. In some other embodiments, the concentration of TiO₂ in the glass-ceramic compositions may be greater than or equal to 2 mol. % and less than or equal to 3 mol. %.

In some embodiments, ZrO₂ may be included in the glass-ceramic compositions. Like TiO₂, ZrO₂ acts as a nucleating agent and aids in the formation of the Li₂Si₂O₅ primary crystal phase upon ceramming. In the embodiments described herein, ZrO₂ is present in the glass-ceramic compositions in a concentration greater than or equal to 0 mol. % and less than or equal to 4 mol. %. In some embodiments, the concentration of ZrO₂ in the glass-ceramic compositions may be greater than or equal to 1 mol. % and less than or equal to 3 mol. %. In some other embodiments, the concentration of ZrO₂ in the glass-ceramic compositions may be greater than or equal to 2 mol. % and less than or equal to 3 mol. %.

Optionally, the glass-ceramic compositions may further include P₂O₅. Like TiO₂ and ZrO₂, P₂O₅ acts as a nucleating agent and aids in the formation of the Li₂Si₂O₅ primary crystal phase upon ceramming. In embodiments where the glass-ceramic compositions contain P₂O₅, P₂O₅ may be present in the glass-ceramic compositions in a concentration of greater than or equal to 0 mol. % and less than or equal to 3 mol. %. In some embodiments, P₂O₅ may be present in the glass-ceramic compositions in a concentration greater than or equal to 0.5 mol. % and less than or equal to 1.5 mol. %.

In the embodiments of the glass-ceramic compositions described herein, a single nucleating agent may be included in the composition (i.e., one of TiO₂, ZrO₂, P₂O₅) or a combination of two or more nucleating agents (i.e., a combination of two or more of TiO₂, ZrO₂, P₂O₅).

The glass-ceramic compositions described herein may optionally include one or more fining agents. The fining agents may include, for example, SnO₂. The fining agents may be present in the glass-ceramic compositions in an amount greater than or equal to about 0 mol. % and less than or equal to about 1.0 mol. %. In exemplary embodiments, the fining agent is SnO₂. SnO₂ may be present in the glass-ceramic compositions in a concentration greater than or equal to about 0 mol. % and less than or equal to about 0.5 mol. %.

In some embodiments described herein, the glass-ceramic compositions are substantially free of heavy metals and compounds containing heavy metals. The term “heavy metals,” as used herein, refers to Ba, As, Sb, Cd, and Pb.

In the embodiments of the glass-ceramic compositions described herein, a ratio of the concentration of Al₂O₃ (mol. %) to the sum of the concentration of alkali oxide R₂O (mol. %) and alkaline earth oxides (mol. %) (i.e., Al₂O₃ (mol. %)/(R₂O (mol. %)+RO (mol. %)) is less than 1. For example, in some embodiments, Al₂O₃ (mol. %)/(R₂O (mol. %)+RO (mol. %)) may be less than 1 and greater than or equal to 0.5. In some of these embodiments Al₂O₃ (mol. %)/(R₂O (mol. %)+RO (mol. %)) may be less than or equal to 0.9, such as less than or equal to 0.8. In some other embodiments Al₂O₃ (mol. %)/(R₂O (mol. %)+RO (mol. %)) may be greater than or equal to 0.5 and less than or equal to 0.75, such as less than or equal to 0.7. It is hypothesized that maintaining the concentrations of constituent components in the glass-ceramic compositions such that the ratio of Al₂O₃ (mol. %)/(R₂O (mol. %)+RO (mol. %) is less than 1 and greater than or equal to 0.5 assists in maintaining the liquidus temperatures and liquidus viscosities within ranges suitable for fusion forming.

In some embodiments of the glass-ceramic compositions described herein the ratio of SiO₂ (mol. %) to Al₂O₃ (mol. %) is greater than 7, such as greater than 7 and less than or equal to 10. In some of these embodiments, the ratio of SiO₂ (mol. %) to Al₂O₃ (mol. %) is greater than 7.1 or even greater than 7.2. In some other embodiments, the ratio of SiO₂ (mol. %) to Al₂O₃ (mol. %) is greater than 7.3.

In some embodiments of the glass-ceramic compositions described herein, the ratio of the sum of the concentration of Li₂O (mol. %) and twice the concentration of SiO₂ (mol. %) to the concentration of Al₂O₃ (mol. %) (i.e., (Li₂O (mol. %)+2*SiO₂ (mol. %))/Al₂O₃ (mol. %)) is greater than 13, such as greater than 13 and less than or equal to 22. In some of these embodiments, the ratio (Li₂O (mol. %)+2*SiO₂ (mol. %))/Al₂O₃ (mol. %) is greater than 14 or even greater than 15, and less than or equal to 22. It is hypothesized that maintaining the concentrations of constituent components in the glass-ceramic compositions such that the ratio (Li₂O (mol. %)+2*SiO₂ (mol. %))/Al₂O₃ (mol. %) is greater than 13 assists in the formation of the primary crystal phase Li₂Si₂O₅. However, if the concentration of Al₂O₃ is too high (i.e., the ratio of (Li₂O (mol. %)+2*SiO₂ (mol. %))/Al₂O₃ (mol. %)) is too low), less of the primary crystal phase Li₂Si₂O₅ will form and, instead, less desirable phases will form, such as solid solutions of eucryptite, stuffed beta-quartz, and/or LiAlSiO₄.

In some embodiments of the glass-ceramic compositions described herein, the ratio of the sum of the concentration of alkali oxide R₂O (mol. %) and twice the concentration SiO₂ (mol. %) to the concentration of Al₂O₃ (mol. %) (i.e., (R₂O (mol. %)+2*SiO₂ (mol. %))/Al₂O₃ (mol. %)) is greater than 8.5. For example, in some embodiments, the ratio (R₂O (mol. %)+2*SiO₂ (mol. %))/Al₂O₃ (mol. %) is greater than 8.5 and less than or equal to 9.5. It is hypothesized that maintaining the concentrations of constituent components in the glass-ceramic compositions such that the ratio (R₂O (mol. %)+2*SiO₂ (mol. %))/Al₂O₃ (mol. %) is greater than 8.5 assists in the formation of the primary crystal phase Li₂Si₂O₅, as described above with the respect to the ratio of (Li₂O (mol. %)+2*SiO₂ (mol. %))/Al₂O₃ (mol. %)). However, it has been found that when the concentrations of Na₂O and K₂O increase relative to Al₂O₃, more Li₂Si₂O₅ is produced and the coefficient of thermal expansion of the glass decreases for a given ceramming schedule.

In some embodiments of the glass-ceramic compositions described herein, the ratio of the sum of the concentration of SiO₂ (mol. %), the concentration of Al₂O₃ (mol. %), the concentration of Li₂O (mol. %), the concentration of K₂O (mol. %), and Na₂O (mol. %) to the sum of the concentration of the nucleating agents (i.e., (SiO₂ (mol. %)+Al₂O₃ (mol. %)+Li₂O (mol. %)+K₂O (mol. %)+Na₂O (mol. %))/(TiO₂ (mol. %)+P₂O₅ (mol. %)+ZrO₂ (mol. %)) is greater than 26, such as greater than 26 and less than or equal to about 31. In some of these embodiments, the ratio may be greater than or equal to about 27, greater than or equal to about 28, or even greater than or equal to about 29. It is hypothesized that maintaining the ratio of (SiO₂ (mol. %)+Al₂O₃ (mol. %)+Li₂O (mol. %)+K₂O (mol. %)+Na₂O (mol. %))/(TiO₂ (mol. %)+P₂O₅ (mol. %)+ZrO₂ (mol. %)) to greater than 26 improves the nucleation of Li₂Si₂O₅. That is, TiO₂, ZrO₂, and P₂O₅ each act as nucleating agents. If the concentration of nucleating agents is too high, less desirable phases will nucleate in the glass, such a rutile and zircon. However, if the concentration of nucleating agents is too low, the glass does not crystallize.

The glass-ceramic compositions described herein have liquidus viscosities suitable for fusion formation, such as by the fusion down-draw process and/or the fusion lamination process. In particular, the glass-ceramic compositions described herein have liquidus viscosities greater than or equal to about 35,000 Poise (35 kPoise). In some embodiments, the liquidus viscosity is greater than or equal to 50 kPoise or even greater than or equal to 100 kPoise.

The glass-ceramic compositions described herein generally have a pre-ceramming average coefficient of thermal expansion CTE_(PC) (i.e., the CTE prior to any treatments which result in the nucleation of ceramic phases in the glass) which is greater than or equal to 65×10⁻⁷/° C. and less than or equal to about 110×10⁻⁷/° C. in a range from 20° C. to 300° C. In some embodiments, the glass-ceramic compositions described herein have a post-ceramming CTE_(AC) of greater than or equal to about 20×10⁻⁷/° C. and less than or equal to about 70×10⁻⁷/° C. in a range from 20° C. to 300° C. In yet other embodiments, the post-ceramming CTE_(AC) of the glass-ceramic compositions may be greater than or equal to about 30×10⁻⁷/° C. and less than or equal to about 70×10⁻⁷/° C. in a range from 20° C. to 300° C.

As noted hereinabove, the glass-ceramic compositions disclosed herein may be treated after formation to induce the nucleation and growth of ceramic phases which, in turn, decreases the coefficient of thermal expansion of the as-formed glass-ceramic. In the embodiments described herein, the treatment to induce the nucleation and growth of ceramic phases in the glass-ceramic composition is a two-part process which includes heating to a nucleation temperature and holding the glass-ceramic composition at this nucleation temperature for a nucleation hold time to begin nucleation of the ceramic phase(s). The second part of the two-part process includes further heating the glass-ceramic composition to a crystallization temperature and holding the glass-ceramic composition at this temperature for a crystallization hold time to allow the nucleated ceramic phases(s) to crystallize and grow. In the embodiments described herein, the nucleation temperature may be from about 700° C. to about 750° C. and the nucleation time may be from about 1 hour to about 2 hours. In the embodiments described herein, the crystallization temperature may be from about 750° C. to about 900° C. and the crystallization hold time may be from about 2 hours to about 24 hours. However, it has now been found that crystallization hold times of greater than 4 hours (e.g., greater than or equal to 6 hours, greater than or equal to 8 hours, greater than or equal to 10 hours, greater than or equal to 12 hours, greater than or equal to 14 hours, greater than or equal to 16 hours, greater than or equal to 18 hours, greater than or equal to 20 hours, greater than or equal to 22 hours, or even greater than or equal to or equal to 24 hours) results in a fewer number of ceramic crystals, each of which are of larger size, than the ceramic crystals produced at crystallization hold times of less than or equal to 4 hours, despite having the same number of nucleants at the beginning of the crystallization phase. These longer crystallization hold times also result in a corresponding decrease in the post-ceramming CTE_(AC). Accordingly, in some embodiments described herein, the glass-ceramic compositions are heat treated at the crystallization temperature for crystallization hold times of greater than 4 hours.

Referring now to FIG. 1, in some embodiments, the glass-ceramic compositions described herein may be used to form the glass clad layers of a laminated glass article, such as the laminated glass article 100 schematically depicted in cross section in FIG. 1. The laminated glass article 100 generally comprises a glass core layer 102 and at least one glass clad layer 104 a. In the embodiment of the laminated glass article 100 shown in FIG. 1 the laminated glass article includes a first glass clad layer 104 a and a second glass clad layer 104 b positioned on opposite sides of the glass core layer 102. While FIG. 1 schematically depicts the laminated glass article 100 as being a laminated glass sheet, it should be understood that other configurations and form factors are contemplated and possible. For example, the laminated glass article may have a non-planar configuration such as a curved glass sheet or the like. Alternatively, the laminated glass article may be a laminated glass tube, container, or the like.

In the embodiment of the laminated glass article 100 depicted in FIG. 1, the glass core layer 102 generally comprises a first surface 103 a and a second surface 103 b which is opposed to the first surface 103 a. A first glass clad layer 104 a is fused to the first surface 103 a of the glass core layer 102 and a second glass clad layer 104 b is fused to the second surface 103 b of the glass core layer 102. The glass clad layers 104 a, 104 b are fused to the glass core layer 102 without any additional non-glass materials, such as adhesives, coating layers or the like, being disposed between the glass core layer 102 and the glass clad layers 104 a, 104 b. Thus, in some embodiments, the glass clad layers 104 a, 104 b are fused directly to the glass core layer 102 or are directly adjacent to the glass core layer. In some embodiments, the laminated glass article 100 comprises one or more intermediate layers disposed between the glass core layer and the glass clad layer(s). For example, the intermediate layers may comprise intermediate glass layers and/or diffusion layers formed at the interface of the glass core layer and the glass clad layer(s) (e.g., by diffusion of one or more components of the glass core and glass clad layers into the diffusion layer). In some embodiments, the laminated glass article comprises a glass-glass laminate (e.g., an in situ fused multilayer glass-glass laminate) in which the interfaces between directly adjacent glass layers are glass-glass interfaces.

In the embodiments of the laminated glass articles described herein, the glass-ceramic composition of the glass clad layers 104 a, 104 b initially produces a CTE match between the glass core layer 102 and the glass clad layers 104 a, 104 b resulting in the formation of little, if any, compressive stress in the glass clad layers 104 a, 104 b. For example, the pre-ceramming CTE_(PC) of the glass clad layers 104 a, 104 b is within about 20%, within about 15%, within about 10%, within about 5%, within about 2%, or within about 1% of the coefficient of thermal expansion of the glass core layer 102. However, after formation, the laminated glass article may be further heat treated to ceram the glass clad layers, thereby creating a CTE mismatch between the glass core layer 102 and the glass clad layers 104 a, 104 b. For example, in the embodiments described herein, the glass clad layers 104 a, 104 b are formed from the glass-ceramic compositions described hereinabove which can be heat treated after formation of the laminated glass article such that the average clad coefficient of thermal expansion CTE_(CL) of the glass clad layers 104 a, 104 b is the glass-ceramic coefficient of expansion CTE_(AC) which is less than the average core coefficient of thermal expansion CTE_(C) of the glass core layer 102. This differential in the coefficients of thermal expansion following heat treatment results in the glass clad layers 104 a, 104 b being compressively stressed without being ion-exchanged or thermally tempered.

For example, in some embodiments, the average core CTE_(C) of the glass core layer 102 may be greater than or equal to about 60×10⁻⁷/° C. in a range from 20° C. to 300° C. In yet other embodiments, the average core CTE_(C) of the glass-ceramic composition of the glass core layer may be greater than or equal to about 80×10⁻⁷/° C. averaged over a range from 20° C. to 300° C. In yet other embodiments, the average core CTE_(C) of the glass-ceramic composition of the glass core layer may be greater than or equal to about 90×10⁻⁷/° C. averaged over a range from 20° C. to 300° C.

In the embodiments described herein, the CTE differential between the glass core layer 102 and the glass clad layers 104 a, 104 b (i.e., |CTE_(C)−CTE_(CL)|) after heat treatment of the laminated glass article 100 as described herein is sufficient to generate a compressive stress in the glass clad layers. In some embodiments the CTE differential between the glass core layer and the glass clad layers is greater than or equal to about 20×10⁻⁷/° C. or even 30×10⁻⁷/° C. In some other embodiments, the CTE differential between the glass core layer and the glass clad layers is greater than or equal to about 40×10⁻⁷/° C. or even 50×10⁻⁷/° C. In yet other embodiments, the CTE differential between the glass core layer and the glass clad layers is greater than or equal to about 60×10⁻⁷/° C. or even 65×10⁻⁷/° C.

In the embodiments described herein the glass core layer may be formed from the exemplary glass core compositions listed in Table 1 below. However, it should be understood that other glass core compositions are contemplated and possible.

TABLE 1 Exemplary Glass Core Compositions Core Example 1 Core Example 2 mol % wt % mol % wt % SiO₂ 69.2 65.9 65 59 Al₂O₃ 8.5 13.7 11.5 17.8 Na₂O 13.9 13.7 13.5 12.7 K₂O 1.2 1.7 3.5 5 MgO 6.5 4.2 5.5 3.3 CaO 0.5 0.5 0.5 0.4 BaO 0 0 0.5 1.2 SnO₂ 0.2 0.4 0.2 0.5

A variety of processes may be used to produce the laminated glass articles described herein including, without limitation, lamination slot draw processes, lamination float processes, or fusion lamination processes. Each of these lamination processes generally involves flowing a first molten glass composition, flowing a second molten glass-ceramic composition, and contacting the first molten glass composition with the second molten glass-ceramic composition at a temperature greater than the glass transition temperature of either composition to form an interface between the two compositions such that the compositions fuse together at the interface as the glass cools and solidifies.

In one particular embodiment, the laminated glass articles 100 described herein may be formed by a fusion lamination process such as the process described in U.S. Pat. No. 4,214,886, which is incorporated herein by reference. Referring to FIG. 2 by way of example, a laminate fusion draw apparatus 200 for forming a laminated glass article includes an upper overflow distributor or isopipe 202 which is positioned over a lower overflow distributor or isopipe 204. The upper overflow distributor 202 includes a trough 210 into which a molten glass-ceramic clad composition 206 (such as the glass-ceramic composition described herein) is fed from a melter (not shown). Similarly, the lower overflow distributor 204 includes a trough 212 into which a molten glass core composition 208 is fed from a melter (not shown).

As the molten glass core composition 208 fills the trough 212, it overflows the trough 212 and flows over the outer forming surfaces 216, 218 of the lower overflow distributor 204. The outer forming surfaces 216, 218 of the lower overflow distributor 204 converge at a root 220. Accordingly, the molten glass core composition 208 flowing over the outer forming surfaces 216, 218 rejoins at the root 220 of the lower overflow distributor 204 thereby forming a glass core layer 102 of a laminated glass article.

Simultaneously, the molten glass-ceramic clad composition 206 overflows the trough 210 formed in the upper overflow distributor 202 and flows over outer forming surfaces 222, 224 of the upper overflow distributor 202. The molten glass-ceramic clad composition 206 is outwardly deflected by the upper overflow distributor 202 such that the molten glass-ceramic clad composition 206 flows around the lower overflow distributor 204 and contacts the molten glass core composition 208 flowing over the outer forming surfaces 216, 218 of the lower overflow distributor, fusing to the molten glass core composition and forming glass clad layers 104 a, 104 b around the glass core layer 102.

While FIG. 2 schematically depicts a particular apparatus for forming planar laminated glass articles such as sheets or ribbons, it should be appreciated that other geometrical configurations are possible. For example, cylindrical laminated glass articles may be formed, for example, using the apparatuses and methods described in U.S. Pat. No. 4,023,953.

In the embodiments described herein, the molten glass core composition 208 generally has an average core coefficient of thermal expansion CTE_(C) which is similar to the average clad coefficient of thermal expansion CTE_(CL) of the molten glass-ceramic clad composition 206. In this embodiment, after the glass core layer 102 and the glass clad layers 104 a, 104 b cool and solidify, the resulting laminated glass article may undergo further processing, such as by heat treatment or the like, in order to ceram at least the glass clad layers 104 a, 104 b which, in turn, changes (i.e., lowers) the CTE of the glass clad layers and results in compressive stress being formed in the glass clad layers 104 a, 104 b of the laminated glass article. For example, when the glass clad layers 104 a, 104 b are formed from a glass-ceramic composition as described herein, heat treating the resultant laminated glass article as described herein lowers the coefficient of thermal expansion CTE_(CL) of the glass clad layers 104 a, 104 b to CTE_(AC), thereby decreasing the clad coefficient of thermal expansion CTE_(CL) relative to the glass core layer 102. The resulting difference in the coefficient of thermal expansion causes compressive stress to develop in the glass clad layers 104 a, 104 b.

EXAMPLES

The embodiments described herein will be further clarified by the following examples.

In order to determine the effect of both composition and heat treatment schedules on the pre-ceramming CTE_(PC) and post-ceramming CTE_(AC), a series of glass samples were made having the compositions listed in Table 2 below. Samples of each composition were initially measured with 3D digital image correlation to determine the coefficient of thermal expansion. 3D digital image correlation is an optical stereo-imaging method that employs tracking and image registration techniques for 3D measurements of changes in images. The technique utilizes a non-contact full field displacement sensor, and relies on viewing 3D displacement of a random pattern on a specimen surface relative to an initial pattern. The random pattern is prepared by airbrushing a high temperature paint speckle pattern on the sample surface. The field of view (FOV) is described by a facet field in which the facets are squares that fill the field. The squares are tens of pixels across in dimension. Images of the sample are taken before and during elevated temperature exposure and are then compared to determine the thermal expansion behavior. As shown in Table 1, the pre-ceramming CTE_(PC) values of the samples were between about 66×10⁻⁷/° C. to about 72×10⁻⁷/° C.

Thereafter, samples of each glass composition listed in Table 2 were cerammed according to the different heat treatment schedules identified in Table 2 and the post-ceramming CTE_(AC) values were measured for the samples. Specifically, the CTE_(AC) data in Table 2 is presented according to the heat treatment schedule the sample was subjected to which is presented using the convention (A ° C., B H) and (Y ° C., Z H), where A is the nucleation temperature, B is the nucleation hold time, Y is the crystallization temperature, and Z is the crystallization hold time. Accordingly, a heat treatment of (700° C., 2 H) (750° C., 24 H) corresponds to a nucleation temperature of 700° C. and a nucleation hold time of 2 hours and a crystallization temperature of 750° C. and a crystallization hold time of 24 hours.

TABLE 2 Exemplary Glass-Ceramic Compositions Mol. % (Wt. %) Ex. A Ex. B Ex. C Ex. D Ex. E Ex. F Ex. G SiO₂ 73.77 (67.78) 73.07 (67.78) 72.35 (67.12) 72.36 (67.46) 72.36 (67.8) 72.37 (68.15) 72 (67.06) Li₂O 5.54 (2.59) 5.62 (2.59) 5.55 (2.56) 5.54 (2.57) 5.56 (2.59) 5.55 (2.6) 5.53 (2.56) Na₂O 4.8 (4.78) 5 (4.78) 5.94 (5.68) 6.93 (6.66) 7.9 (7.64) 8.9 (8.64) 7.87 (7.56) K₂O 2.69 (4.37) 3.01 (4.37) 2.98 (4.33) 1.98 (2.9) 0.99 (1.46) 0 (0) 0.99 (1.44) TiO₂ 2.38 (2.96) 2.4 (2.96) 2.38 (2.94) 2.38 (2.95) 2.38 (2.97) 2.38 (2.98) 2.37 (2.93) ZrO₂ 0.78 (1.52) 0.8 (1.52) 0.79 (1.51) 0.8 (1.52) 0.79 (1.52) 0.79 (1.53) 0.79 (1.51) SnO₂ 0.1 (0.23) 0.1 (0.23) 0.1 (0.23) 0.1 (0.23) 0.1 (0.23) 0.1 (0.23) 0.1 (0.23) Al₂O₃ 10 (15.76) 10.01 (15.76) 9.91 (15.6) 9.91 (15.68) 9.91 (15.76) 9.91 (15.84) 9.86 (15.59) P₂O₅ 0 (0) 0 (0) 0 (0) 0 (0) 0 (0) 0 (0) 0.5 (1.09) Liquidus 172,696 Viscosity (P) CTE_(PC) 68.9 67.2 71.9 71 70.2 66.9 70.3 (×10⁻⁷/° C.) CTE_(AC) 57.7 37.5 27.7 19.1 (×10⁻⁷/° C.) (700° C., 2 H) (750° C., 24 H) CTE_(AC) 53.2 45.8 36.2 37.5 25.4 41.1 (×10⁻⁷/° C.) (750° C., 2 H) (800° C., 24 H) CTE_(AC) 53.2 69.6 40.3 35.6 27.4 35.4 (×10⁻⁷/° C.) (750° C., 2 H) (825° C., 12 H) CTE_(AC) 53.4 46.7 38.7 30.1 40.5 (×10⁻⁷/° C.) (750° C., 2 H) (850° C., 12 H) CTE_(AC) 52.2 49.1 39.3 30.5 40.6 (×10⁻⁷/° C.) (750° C., 2 H) (850° C., 16 H) CTE_(AC) 55.7 34.9 (×10⁻⁷/° C.) (750° C., 2 H) (900° C., 2 H) CTE_(AC) 55 31.2 (×10⁻⁷/° C.) (750° C., 2 H) (900° C., 4 H) Al₂O₃/(RO + R₂O) 0.8 (1.3) 0.7 (1.3) 0.7 (1.2) 0.5 (1.3) 0.5 (1.3) 0.7 (1.4) 0.5 (1.3) SiO₂/Al₂O₃ 7 (4) 7 (4) 10 (4) 10 (4) 10 (4) 7 (4) 10 (4) (Li₂O + 2*SiO₂)/Al₂O₃ 15 (9) 15 (11) 22 (11) 22 (11) 22 (11) 15 (11) 22 (11) (R₂O + 2*SiO₂)/Al₂O₃ 16 (9) 16 (9) 23 (9) 23 (9) 23 (9) 16 (9) 23 (9) (SiO₂ + Al₂O₃ + 31 (21) 30 (21) 30 (21) 30 (21) 30 (21) 31 (21) 26 (17) Li₂O + K₂O + Na₂O)/ (TiO₂ + ZrO₂ + P₂O₅)

As shown in Table 2, heat treatment of the glass-ceramic samples generally lowered the coefficient of thermal expansion of each sample relative to the pre-ceramming CTE_(PC). The post-ceramming CTE_(AC) is dependent on the type, quantity, and distribution of crystalline phases in the glass-ceramic samples. In the glass-ceramic samples of Examples A-G, the primary crystalline phase present after heat treatment was Li₂Si₂O₅ with a secondary phase of rutile (TiO₂). The quantity of both crystalline phases was dependent on the time and temperature of the treatment conditions as well as the glass-ceramic composition. In particular, it was determined that greater concentrations of Na₂O relative to the concentration of K₂O resulted in the nucleation and crystallization of more of the Li₂Si₂O₅ phase which, in turn, provided a more pronounced decrease in the post-ceramming CTE_(AC).

In addition, it was also observed that for two samples formed from the same glass-ceramic composition and heat treated at a given nucleation temperature and nucleation hold time and thereafter heat treated at the same crystallization temperature but for different crystallization hold times, the sample heat treated for the longer crystallization hold time actually had fewer (albeit larger) ceramic crystals after crystallization than the sample heat treated for the shorter crystallization hold time, despite both samples having approximately the same number of nucleants after the initial nucleation phase of the heat treatment.

It should now be understood that the glass-ceramic compositions described herein have a post-ceramming CTE_(AC) that is less than the pre-ceramming CTE_(PC) and, as such, the glass-ceramic compositions are well suited for use as glass clad layers of strengthened laminated glass articles.

When the glass-ceramic compositions are used to produce laminated glass articles, the laminated glass articles can be used for a variety of applications including, for example, for cover glass or glass backplane applications in consumer or commercial electronic devices including, for example, LCD, LED, OLED, and quantum dot displays, computer monitors, and automated teller machines (ATMs); for touch screen or touch sensor applications, for portable electronic devices including, for example, mobile telephones, personal media players, and tablet computers; for integrated circuit applications including, for example, semiconductor wafers; for photovoltaic applications; for architectural glass applications; for automotive or vehicular glass applications; for commercial or household appliance applications; for lighting or signage (e.g., static or dynamic signage) applications; or for transportation applications including, for example, rail and aerospace applications.

It will be apparent to those skilled in the art that various modifications and variations can be made to the embodiments described herein without departing from the spirit and scope of the claimed subject matter. Thus it is intended that the specification cover the modifications and variations of the various embodiments described herein provided such modification and variations come within the scope of the appended claims and their equivalents. 

What is claimed is:
 1. A glass-ceramic composition comprising: from about 60 mol. % to about 75 mol. % SiO₂; from about 5 mol. % to about 10 mol. % Al₂O₃; from about 2 mol. % to about 20 mol. % alkali oxide R₂O, the alkali oxide R₂O comprising Li₂O and Na₂O, wherein the alkali oxide R₂O comprises from about 1 mol. % to about 10 mol. % Li₂O; from 0 mol. % to about 5 mol. % alkaline earth oxide RO, the alkaline earth oxide RO comprising MgO; a ratio of Al₂O₃ (mol. %)/(R₂O (mol. %)+RO (mol. %)) of less than 1; a major crystalline phase of Li₂Si₂O₅; and a liquidus viscosity of greater than 35 kP.
 2. The glass-ceramic composition of claim 1, wherein the alkali oxide R₂O comprises from about 1 mol. % to about 10 mol. % Na₂O.
 3. The glass-ceramic composition of claim 1, wherein the alkaline earth oxide RO comprises greater than 0 mol. % and up to about 5 mol. % MgO.
 4. The glass-ceramic composition of claim 1, further comprising from greater than zero mol. % to about 4 mol. % of a nucleating agent selected from the group consisting of TiO₂, ZrO₂, P₂O₅, and combinations thereof.
 5. The glass-ceramic composition of claim 4, comprising from about 1 mol. % to about 4 mol. % TiO₂.
 6. The glass-ceramic composition of claim 4, comprising ZrO₂ in an amount up to about 4 mol. %.
 7. The glass-ceramic composition of claim 4, wherein a ratio of (SiO₂ (mol. %)+Al₂O₃ (mol. %)+Li₂O (mol. %)+K₂O (mol. %)+Na₂O (mol. %))/(TiO₂ (mol. %)+P₂O₅ (mol. %)+ZrO₂ (mol. %)) is greater than
 26. 8. The glass-ceramic composition of claim 7, wherein the ratio of (SiO₂ (mol. %)+Al₂O₃ (mol. %)+Li₂O (mol. %)+K₂O (mol. %)+Na₂O (mol. %))/(TiO₂ (mol. %)+P₂O₅ (mol. %)+ZrO₂ (mol. %)) is less than
 31. 9. The glass-ceramic composition of claim 1, wherein a ratio of SiO₂ (mol. %) to Al₂O₃ (mol. %) is greater than
 7. 10. The glass-ceramic composition of claim 1, wherein a ratio of (Li₂O (mol. %)+2*SiO₂ (mol. %))/Al₂O₃ (mol. %) is greater than
 13. 11. The glass-ceramic composition of claim 1, wherein a ratio of (R₂O (mol. %)+2*SiO₂ (mol. %))/Al₂O₃ (mol. %) is greater than 8.5.
 12. The glass-ceramic composition of claim 1, further comprising K₂O in an amount up to about 10 mol. %.
 13. The glass-ceramic composition of claim 1, wherein the liquidus viscosity is greater than or equal to about 100 kP.
 14. The glass-ceramic composition of claim 1, wherein the glass-ceramic composition has a pre-ceramming CTE_(PC) of greater than or equal to about 65×10⁻⁷/° C. and less than or equal to about 110×10⁻⁷/° C.
 15. The glass-ceramic composition of claim 1, wherein the glass-ceramic composition has a post-ceramming CTE_(AC) of greater than or equal to 20×10⁻⁷/° C. and less than or equal to about 70×10⁻⁷/° C. 